Elastic Film Compositions with Improved Tear Resistance

ABSTRACT

A film composition comprising one or more propylene-based polymers and one or more hydrocarbon resins, and methods for making the same are provided. The propylene-based polymer may have (i) 60 wt % or more units derived from propylene, (ii) isotactically arranged propylene derived sequences, and (iii) a heat of fusion less than 65 J/g. The hydrocarbon resin may have a glass transition temperature greater than 20° C.

BACKGROUND OF THE INVENTION

1. Field of the Invention

Embodiments of the present invention generally relate to propylene-basedpolymers and films made therefrom. More particularly, embodiments of thepresent invention relate to films of propylene-based polymers havingincreased tear resistance.

2. Description of the Related Art

Materials with good stretchability and elasticity are used tomanufacture a variety of disposable articles in addition to durablearticles including incontinence pads, disposable diapers, trainingpants, clothing, undergarments, sports apparel, automotive trim,weather-stripping, gaskets, and furniture upholstery. For clothing,stretchability and elasticity are performance attributes that allow thematerials to provide a closely conforming fit to the body of the wearer.Various types of elastic laminates have been used for such materials.

Elastic laminates, especially those used as diaper waist bands, legcuffs, and elastic stretch engines, are intended to contact the weareror user. As such, comfort is a primary design consideration. The comfortfactor is a direct result of the stretchability and elasticity of thefilm; however, the stretchability and elasticity of the film usuallycomes with a price. As the stretchability and elasticity of the filmincrease, the films become less durable and more susceptible to tear.

There is a need, therefore, for improving the tear resistance of a filmwithout compromising physical and elastic properties.

SUMMARY OF THE INVENTION

Film compositions and methods for making the same are provided. In atleast one specific embodiment, the film can include one or morepropylene-based polymers and one or more hydrocarbon resins. Thepropylene-based polymer can include (i) 60 wt % or more units derivedfrom propylene, (ii) isotactically arranged propylene derived sequences,and (iii) a heat of fusion less than 65 J/g. The hydrocarbon resin canhave a glass transition temperature greater than 20° C.

In at least one other specific embodiment, the film can include one ormore propylene-based polymers having 60 wt % or more units derived frompropylene, isotactically arranged propylene derived sequences, a heat offusion less than 45 J/g, a density of at least 0.80 g/cm³, and a MFR ofat least 3.0 g/10 min; and one or more hydrogenated cycloaliphatic resineach having a molecular weight (Mn) of from 200 to 5,000 and a glasstransition temperature greater than 20° C., wherein the amount of thehydrocarbon resin in the composition is sufficient to increase intrinsictear of the film by at least 5%.

In at least one specific embodiment, the method for making the filmcomposition can include admixing one or more propylene-based polymersand one or more miscible hydrocarbon resins in an amount sufficient toprovide a film having an increase in intrinsic tear by at least 5%compared to a film without either the one or more propylene-basedpolymers or the one or more miscible hydrocarbon resins. Thepropylene-based polymer can include (i) 60 wt % or more units derivedfrom propylene, (ii) isotactically arranged propylene derived sequences,and (iii) a heat of fusion less than 65 J/g. The hydrocarbon resin canhave a glass transition temperature greater than 20° C.

DETAILED DESCRIPTION OF THE INVENTION

Films having significantly increased tear resistance with excellentstretchability and elasticity and methods for producing the same areprovided. In one or more embodiments, the film includes one or morepropylene-based polymers and one or more hydrocarbon resins. The filmcan further include polypropylene and/or one or more thermoplasticresins. In one or more embodiments, the film can include one or morerubber components and/or one or more additives. Preferably, the variouscomponents of the film are selected such that the film has an intrinsictear of at least 1.5 gm/micron and preferably at least 3.9 gm/micron,and an elongation at break of at least 500%.

Propylene-Based Polymer

The propylene-based polymer can be propylene-α-olefin-diene terpolymersor propylene-α-olefin copolymers. For simplicity and ease ofdescription, however, the term “propylene-based polymer” as used hereinrefers to both propylene-α-olefin-diene terpolymers andpropylene-α-olefin copolymers.

The propylene-based polymer can be prepared by polymerizing propylenewith one or more comonomers. In at least one specific embodiment, thepropylene-based polymer can be prepared by polymerizing propylene withone or more dienes. In at least one other specific embodiment, thepropylene-based polymer can be prepared by polymerizing propylene withethylene and/or at least one C₄-C₂₀ α-olefin, or a combination ofethylene and at least one C₄-C₂₀ α-olefin and one or more dienes. Theone or more dienes can be conjugated or non-conjugated. Preferably, theone or more dienes are non-conjugated.

The comonomers can be linear or branched. Preferred linear comonomersinclude ethylene or C₄ to C₈ α-olefins, more preferably ethylene,1-butene, 1-hexene, and 1-octene, even more preferably ethylene or1-butene. Preferred branched comonomers include 4-methyl-1-pentene,3-methyl-1-pentene, and 3,5,5-trimethyl-1-hexene. In one or moreembodiments, the comonomer can include styrene.

Illustrative dienes can include, but are not limited to,5-ethylidene-2-norbornene (ENB); 1,4-hexadiene; 5-methylene-2-norbornene(MNB); 1,6-octadiene; 5-methyl-1,4-hexadiene;3,7-dimethyl-1,6-octadiene; 1,3-cyclopentadiene; 1,4-cyclohexadiene;vinyl norbornene (VNB); dicyclopendadiene (DCPD), and combinationsthereof. Preferably, the diene is ENB.

Preferred methods and catalysts for producing the propylene-basedpolymers are found in publications US 2004/0236042 and WO 05/049672 andin U.S. Pat. No. 6,881,800, which are all incorporated by referenceherein. Pyridine amine complexes, such as those described in WO03/040201 are also useful to produce the propylene-based polymers usefulherein. The catalyst can involve a fluxional complex, which undergoesperiodic intra-molecular re-arrangement so as to provide the desiredinterruption of stereoregularity as in U.S. Pat. No. 6,559,262. Thecatalyst can be a stereorigid complex with mixed influence on propyleneinsertion, see Rieger EP 1070087. The catalyst described in EP 1614699may also be used for the production of backbones suitable for theinvention.

The propylene-based polymer can have an average propylene content on aweight percent basis of from about 60 wt % to about 99.7 wt %, morepreferably from about 60 wt % to about 99.5 wt %, more preferably fromabout 60 wt % to about 97 wt %, more preferably from about 60 wt % toabout 95 wt % based on the weight of the polymer. In one embodiment, thebalance comprises diene. In another embodiment, the balance comprisesone or more dienes and one or more of the α-olefins describedpreviously. Other preferred ranges are from about 80 wt % to about 95 wt% propylene, more preferably from about 83 wt % to about 95 wt %propylene, more preferably from about 84 wt % to about 95 wt %propylene, and more preferably from about 84 wt % to about 94 wt %propylene based on the weight of the polymer. The balance of thepropylene-based polymer comprises a diene and optionally, one or morealpha-olefins. In one or more embodiments above or elsewhere herein, thealpha-olefin is butene, hexene or octene. In other embodiments, twoalpha-olefins are present, preferably ethylene and one of butene, hexeneor octene.

Preferably, the propylene-based polymer comprises about 0.3 wt % toabout 24 wt % of a non-conjugated diene, based on the weight of thepolymer, more preferably from about 0.5 wt % to about 12 wt %, morepreferably about 0.6 wt % to about 8 wt %, and more preferably about 0.7wt % to about 5 wt %. In other embodiments, the diene content rangesfrom about 0.3 wt % to about 10 wt %, more preferably from about 0.3 toabout 5 wt %, more preferably from about 0.3 wt % to about 4 wt %,preferably from about 0.3 wt % to about 3.5 wt %, preferably from about0.3 wt % to about 3.0 wt %, and preferably from about 0.3 wt % to about2.5 wt % based on the weight of the polymer. In one or more embodimentsabove or elsewhere herein, the propylene-based polymer comprises ENB inan amount of from about 0.5 to about 4 wt %, more preferably from about0.5 to about 2.5 wt %, and more preferably from about 0.5 to about 2.0wt %.

In other embodiments, the propylene-based polymer preferably comprisespropylene and diene in one or more of the ranges described above withthe balance comprising one or more C₂ and/or C₄-C₂₀ olefins. In general,this will amount to the propylene-based polymer preferably comprisingfrom about 5 to about 40 wt % of one or more C₂ and/or C₄-C₂₀ olefinsbased the weight of the polymer. When C₂ and/or a C₄-C₂₀ olefins arepresent the combined amounts of these olefins in the polymer ispreferably at least about 5 wt % and falling within the ranges describedherein. Other preferred ranges for the one or more α-olefins includefrom about 5 wt % to about 35 wt %, more preferably from about 5 wt % toabout 30 wt %, more preferably from about 5 wt % to about 25 wt %, morepreferably from about 5 wt % to about 20 wt %, more preferably fromabout 5 to about 17 wt % and more preferably from about 5 wt % to about16 wt %.

The propylene-based polymer can have a weight average molecular weight(Mw) of 5,000,000 or less, a number average molecular weight (Mn) ofabout 3,000,000 or less, a z-average molecular weight (Mz) of about10,000,000 or less, and a g′ index of 0.95 or greater measured at theweight average molecular weight (Mw) of the polymer using isotacticpolypropylene as the baseline, all of which can be determined by sizeexclusion chromatography, e.g., 3D SEC, also referred to as GPC-3D, asdescribed herein.

In one or more embodiments above or elsewhere herein, thepropylene-based polymer can have a Mw of about 5,000 to about 5,000,000g/mole, more preferably a Mw of about 10,000 to about 1,000,000, morepreferably a Mw of about 20,000 to about 500,000, or more preferably aMw of about 50,000 to about 400,000, wherein Mw is determined asdescribed herein.

In one or more embodiments above or elsewhere herein, thepropylene-based polymer can have a Mn of about 2,500 to about 2,500,000g/mole, more preferably a Mn of about 5,000 to about 500,000, morepreferably a Mn of about 10,000 to about 250,000, or more preferably aMn of about 25,000 to about 200,000, wherein Mn is determined asdescribed herein.

In one or more embodiments above or elsewhere herein, thepropylene-based polymer can have a Mz of about 10,000 to about 7,000,000g/mole, more preferably a Mz of about 50,000 to about 1,000,000, morepreferably a Mz of about 80,000 to about 700,000, or more preferably aMz of about 100,000 to about 500,000, wherein Mz is determined asdescribed herein.

The molecular weight distribution index (MWD=(Mw/Mn)), sometimesreferred to as a “polydispersity index” (PDI), of the propylene-basedpolymer can be from about 1.5 to about 40. In some embodiments, the MWDcan have an upper limit of 40, or 20, or 10, or 5, or 4.5, and a lowerlimit of 1.5, or 1.8, or 2.0. In one or more embodiments above orelsewhere herein, the MWD of the propylene-based polymer is about 1.8 to5 and most preferably about 1.8 to 3. Techniques for determining themolecular weight (Mn and Mw) and molecular weight distribution (MWD) canbe found in U.S. Pat. No. 4,540,753 (Cozewith, Ju and Verstrate) (whichis fully incorporated herein by reference for purposes of U.S.practices) and references cited therein, in Macromolecules, 1988, volume21, pg. 3360 (Verstrate et al.) (which is fully incorporated herein byreference for purposes of U.S. practice), and references cited therein,and in accordance with the procedures disclosed in U.S. Pat. No.6,525,157, column 5, lines 1-44, which patent is fully incorporatedherein by reference.

In one or more embodiments above or elsewhere herein, thepropylene-based polymer can have a g′ index value of 0.95 or greater,preferably at least 0.98, with at least 0.99 being more preferred,wherein g′ is measured at the Mw of the polymer using the intrinsicviscosity of isotactic polypropylene as the baseline. For use herein,the g′ index is defined as:

$g^{\prime} = \frac{\eta_{b}}{\eta_{l}}$

where η_(b) is the intrinsic viscosity of the propylene-based polymerand η_(t) is the intrinsic viscosity of a linear polymer of the sameviscosity-averaged molecular weight (M_(v)) as the propylene-basedpolymer. η_(t)=KM_(v) ^(α), where K and α are measured values for linearpolymers and should be obtained on the same instrument as the one usedfor the g′ index measurement.

In one or more embodiments above or elsewhere herein, thepropylene-based polymer may have a density of about 0.85 g/cm³ to about0.92 g/cm³, more preferably, about 0.87 g/cm³ to 0.90 g/cm³, morepreferably about 0.88 g/cm³ to about 0.89 g/cm³ at room temperature asmeasured per the ASTM D-1505 test method.

In one or more embodiments above or elsewhere herein, thepropylene-based polymer may have a melt flow rate (MFR, 2.16 kg weight(230° C.), equal to or greater than 0.2 g/10 min as measured accordingto the ASTM D-1238(A) test method as modified (described below).Preferably, the MFR (2.16 kg (230° C.) is from about 0.5 g/10 min toabout 200 g/10 min and more preferably from about 1 g/10 min to about100 g/10 min. In some embodiments, the propylene-based polymer has anMFR of 0.5 g/10 min to 200 g/10 min, especially from 2 g/10 min to 30g/10 min, more preferably from 5 g/10 min to 30 g/10 min, morepreferably 10 g/10 min to 30 g/10 min or more especially 10 g/10 min toabout 25 g/10 min.

The propylene-based polymer may have a Mooney viscosity ML (1+4) 125°C., as determined according to ASTM D-1646, of less than 100, morepreferably less than 75, even more preferably less than 60, mostpreferably less than 30.

In one or more embodiments above or elsewhere herein, thepropylene-based polymer may have a heat of fusion (Hf) determinedaccording to the DSC procedure described below which is greater than orequal to about 0.5 Joules per gram (J/g), and is ≦about 80 J/g,preferably ≦about 75 J/g, preferably ≦about 70 J/g, more preferably≦about 60 J/g, more preferably ≦about 50 J/g, more preferably ≦about 45J/g. Also preferably, the propylene-based polymer has a heat of fusionthat is greater than or equal to about 1 J/g, preferably greater than orequal to about 5 J/g. In another embodiment, the propylene-based polymercan have a heat of fusion (Hf) which is from about 0.5 J/g to about 75J/g, preferably from about 1 J/g to about 75 J/g, more preferably fromabout 0.5 J/g to about 35 J/g. Preferred propylene-based polymers andcompositions can be characterized in terms of both their melting points(Tm) and heats of fusion, which properties can be influenced by thepresence of comonomers or steric irregularities that hinder theformation of crystallites by the polymer chains. In one or moreembodiments, the heat of fusion ranges from a lower limit of 1.0 J/g, or1.5 J/g, or 3.0 J/g, or 4.0 J/g, or 6.0 J/g, or 7.0 J/g, to an upperlimit of 30 J/g, or 35 J/g, or 40 J/g, or 50 J/g, or 60 J/g or 70 J/g,or 75 J/g, or 80 J/g.

The crystallinity of the propylene-based polymer can also be expressedin terms of percentage of crystallinity (i.e. % crystallinity). In oneor more embodiments above or elsewhere herein, the propylene-basedpolymer has a % crystallinity of from 0.5% to 40%, preferably 1% to 30%,more preferably 5% to 25% wherein % crystallinity is determinedaccording to the DSC procedure described below. In another embodiment,the propylene-based polymer preferably has a crystallinity of less than40%, preferably about 0.25% to about 25%, more preferably from about0.5% to about 22%, and most preferably from about 0.5% to about 20%. Asdisclosed above, the thermal energy for the highest order ofpolypropylene is estimated at 189 J/g (i.e., 100% crystallinity is equalto 189 J/g.).

In addition to this level of crystallinity, the propylene-based polymerpreferably has a single broad melting transition. However, thepropylene-based polymer can show secondary melting peaks adjacent to theprincipal peak, but for purposes herein, such secondary melting peaksare considered together as a single melting point, with the highest ofthese peaks (relative to a baseline as described herein) beingconsidered the melting point of the propylene-based polymer.

The propylene-based polymer preferably has a melting point (measured byDSC) of equal to or less than 100° C., preferably less than 90° C.,preferably less than 80° C., more preferably less than or equal to 75°C., preferably from about 25° C. to about 80° C., preferably about 25°C. to about 75° C., more preferably about 30° C. to about 65° C.

The Differential Scanning Calorimetry (DSC) procedure can be used todetermine heat of fusion and melting temperature of the propylene-basedpolymer. The method is as follows: about 0.5 grams of polymer is weighedout and pressed to a thickness of about 15-20 mils (about 381-508microns) at about 140° C.-150° C., using a “DSC mold” and Mylar as abacking sheet. The pressed pad is allowed to cool to ambient temperatureby hanging in air (the Mylar is not removed). The pressed pad isannealed at room temperature (23-25° C.) for about 8 days. At the end ofthis period, a disc of about 15-20 mg is removed from the pressed padusing a punch die and is placed in a 10 microliter aluminum sample pan.The sample is placed in a Differential Scanning Calorimeter (PerkinElmer Pyris 1 Thermal Analysis System) and is cooled to about −100° C.The sample is heated at 10° C./min to attain a final temperature ofabout 165° C. The thermal output, recorded as the area under the meltingpeak of the sample, is a measure of the heat of fusion and can beexpressed in Joules per gram of polymer and is automatically calculatedby the Perkin Elmer System. The melting point is recorded as thetemperature of the greatest heat absorption within the range of meltingof the sample relative to a baseline measurement for the increasing heatcapacity of the polymer as a function of temperature.

The propylene-based polymer can have a triad tacticity of threepropylene units, as measured by ¹³C NMR, of 75% or greater, 80% orgreater, 82% or greater, 85% or greater, or 90% or greater. Preferredranges include from about 50 to about 99%, more preferably from about 60to about 99%, more preferably from about 75 to about 99% and morepreferably from about 80 to about 99%; and in other embodiments fromabout 60 to about 97%. Triad tacticity is determined by the methodsdescribed in U.S. Patent Application Publication 2004/0236042.

In one or more embodiments above or elsewhere herein, thepropylene-based polymer can be a blend of discrete randompropylene-based polymers. Such blends can include ethylene-basedpolymers and propylene-based polymers, or at least one of each suchethylene-based polymers and propylene-based polymers. The number ofpropylene-based polymers can be three or less, more preferably two orless.

In one or more embodiments above or elsewhere herein, thepropylene-based polymer can include a blend of two propylene-basedpolymers differing in the olefin content, the diene content, or both.

In one or more embodiments above or elsewhere herein, thepropylene-based polymer can include a propylene based elastomericpolymer produced by random polymerization processes leading to polymershaving randomly distributed irregularities in stereoregular propylenepropagation. This is in contrast to block copolymers in whichconstituent parts of the same polymer chains are separately andsequentially polymerized.

In another embodiment, the propylene-based polymers can includecopolymers prepared according the procedures in WO 02/36651. Likewise,the propylene-based polymer can include polymers consistent with thosedescribed in WO 03/040201, WO 03/040202, WO 03/040095, WO 03/040201, WO03/040233, and/or WO 03/040442. Additionally, the propylene-basedpolymer can include polymers consistent with those described in EP 1 233191, and U.S. Pat. No. 6,525,157, along with suitable propylene homo-and copolymers described in U.S. Pat. No. 6,770,713 and U.S. PatentApplication Publication 2005/215964, all of which are fully incorporatedherein by reference. The propylene-based polymer can also include one ormore polymers consistent with those described in EP 1 614 699 or EP 1017 729.

Grafted (Functionalized) Backbone

In one or more embodiments, the propylene-based polymer can be grafted(i.e., “functionalized”). As used herein, the term “grafting” denotescovalent bonding of the grafting monomer to a polymer chain of thepropylene-based polymer. The grafting monomer can be one or moreethylenically unsaturated carboxylic acids or acid derivatives, such asan acid anhydride, ester, salt, amide, imide, acrylates or the like.Illustrative grafting monomers include but are not limited to acrylicacid, methacrylic acid, maleic acid, fumaric acid, itaconic acid,citraconic acid, mesaconic acid, maleic anhydride, 4-methylcyclohexene-1,2-dicarboxylic acid anhydride,bicyclo(2.2.2)octene-2,3-dicarboxylic acid anhydride,1,2,3,4,5,8,9,10-octahydronaphthalene-2,3-dicarboxylic acid anhydride,2-oxa-1,3-diketospiro(4.4)nonene, bicyclo(2.2.1)heptene-2,3-dicarboxylicacid anhydride, maleopimaric acid, tetrahydrophtalic anhydride,norbornene-2,3-dicarboxylic acid anhydride, nadic anhydride, methylnadic anhydride, himic anhydride, methyl himic anhydride, andx-methylbicyclo(2.2.1)heptene-2,3-dicarboxylic acid anhydride. Othersuitable grafting monomers include methyl acrylate and higher alkylacrylates, methyl methacrylate and higher alkyl methacrylates, acrylicacid, methacrylic acid, hydroxy-methyl methacrylate, hydroxyl-ethylmethacrylate and higher hydroxy-alkyl methacrylates and glycidylmethacrylate. Maleic anhydride is a preferred grafting monomer.

In one or more embodiments, the grafted propylene based polymer includesabout 0.5 to about 10 wt % ethylenically unsaturated carboxylic acid oracid derivative, more preferably from about 0.5 to about 6 wt %, morepreferably from about 0.5 to about 3 wt %; in other embodiments fromabout 1 to about 6 wt %, more preferably from about 1 to about 3 wt %.In a preferred embodiment wherein the graft monomer is maleic anhydride,the maleic anhydride concentration in the grafted polymer is preferablyin the range of about 1 to about 6 wt %, preferably at least about 0.5wt % and highly preferably about 1.5 wt %.

Styrene and derivatives thereof such as paramethyl styrene, or otherhigher alkyl substituted styrenes such as t-butyl styrene can be used asa charge transfer agent in the presence of the grafting monomer toinhibit chain scission. This allows further minimization of the betascission reaction and the production of a higher molecular weightgrafted polymer (MFR equal to about 1.5).

Preparing Grafted Propylene-Based Polymers

The grafted propylene-based polymer can be prepared using conventionaltechniques. For example, the graft polymer can be prepared in solution,in a fluidized bed reactor, or by melt grafting. A preferred graftedpolymer can be prepared by melt blending in a shear-imparting reactor,such as an extruder reactor. Single screw or twin screw extruderreactors such as co-rotating intermeshing extruder or counter-rotatingnon-intermeshing extruders, and co-kneaders such as those sold by Bussare also preferred.

In one or more embodiments, the grafted polymer can be prepared by meltblending the ungrafted propylene-based polymer with a free radicalgenerating catalyst, such as a peroxide inititator, in the presence ofthe grafting monomer. The preferred sequence for the grafting reactionincludes melting the propylene-based polymer, adding and dispersing thegrafting monomer, introducing the peroxide and venting the unreactedmonomer and by-products resulting from the peroxide decomposition. Othersequences can include feeding the monomers and the peroxidepre-dissolved in a solvent.

Illustrative peroxide initiators include but are not limited to: diacylperoxides such as benzoyl peroxide; peroxyesters such as tert-butylperoxy benzoate, tert-butylperoxy acetate,00-tert-butyl-0-(2-ethylhexyl)monoperoxy carbonate; peroxyketals such asn-butyl-4,4-di-(tert-butyl peroxy) valerate; and dialkyl peroxides suchas 1,1-bis(tertbutylperoxy) cyclohexane,1,1-bis(tert-butylperoxy)-3,3,5-trimethylcyclohexane,2,2-bis(tert-butylperoxy)butane, dicumyl-peroxide,tert-butylcumylperoxide, di-(2-tert-butylperoxy-isopropyl-(2))benzene,di-tert-butylperoxide (DTBP),2,5-dimethyl-2,5-di(tert-butylperoxy)-hexane,2,5-dimethyl-2,5-di(tert-butylperoxy)-hexyne, 3,3,5,7,7-pentamethyl1,2,4-trioxepane; and the like.

Hydrocarbon Resin

The one or more hydrocarbon resins may be grafted or ungrafted.Optionally, the resin may be hydrogenated. Preferably, the one or morehydrocarbon resins are low molecular weight hydrocarbon(s) that arecompatible with the core layer. The resin may have a number averagemolecular weight (Mn) less than about 5000, preferably less than about2000, most preferably in the range of from about 500 to about 1000. Theresin may be natural or synthetic and, in some embodiments, may have asoftening point in the range of from about 60° C. to about 180° C.

Suitable hydrocarbon resins can include, but are not limited to,petroleum resins, terpene resins, styrene resins, and cyclopentadieneresins. In one or more embodiments, the hydrocarbon resin is selectedfrom the group consisting of aliphatic hydrocarbon resins, hydrogenatedaliphatic hydrocarbon resins, aliphatic/aromatic hydrocarbon resins,hydrogenated aliphatic/aromatic hydrocarbon resins, cycloaliphatichydrocarbon resins, hydrogenated cycloaliphatic resins,cycloaliphatic/aromatic hydrocarbon resins, hydrogenatedcycloaliphatic/aromatic hydrocarbon resins, hydrogenated aromatichydrocarbon resins, polyterpene resins, terpene-phenol resins, rosinsand rosin esters, hydrogenated rosins and rosin esters, and combinationsthereof.

Suitable hydrocarbon resins include EMPR 120, 104, 111, 106, 112, and115, EMFR 100 and 10A, ECR-373 and ESCOREZ® 2101, 2203, 2520, 5380,5600, 5618, and 5690 (commercially available from ExxonMobil ChemicalCompany of Baytown, Tex., USA); ARKON™ M90, M100, M115 and M135 andSUPER ESTER™ rosin esters (commercially available from Arakawa ChemicalCompany of Japan); SYLVARES™ phenol modified styrene, methyl styreneresins, and styrenated terpene resins, ZONATAC™ terpene-aromatic resins,and terpene phenolic resins (commercially available from ArizonaChemical Company of Jacksonville, Fla., USA); SYLVATAC™ and SYLVALITE™rosin esters (commercially available from Arizona Chemical Company ofJacksonville, Fla., USA); NORSOLENE™ aliphatic aromatic resins(commercially available from Cray Valley of France); DERTOPHENE™ terpenephenolic resins (commercially available from DRT Chemical Company ofLandes, France); EASTOTAC™ resins, PICCOTAC™ C₅/C₉ resins, REGALITE™ andREGALREZ™ aromatic and REGALITE™ cycloaliphatic/aromatic resins(commercially available from Eastman Chemical Company of Kingsport,Tenn.); WINGTACK™ ET and EXTRA™ (commercially available from Sartomer ofExton, Pa., USA); FORAL™, PENTALYN™, and PERMALYN™ rosins and rosinesters (commercially available from Hercules, now Eastman ChemicalCompany of Kingsport, Tenn., USA); QUINTONE™ acid modified C₅ resins,C₅/C₉ resins, and acid modified C₅/Cg resins (commercially availablefrom Nippon Zeon of Japan); LX™ mixed aromatic/cycloaliphatic resins(commercially available from Neville Chemical Company of Pittsburgh,Pa., USA); CLEARON™ hydrogenated terpene aromatic resins (commerciallyavailable from Yasuhara of Japan); and PICCOLYTE™ (commerciallyavailable from Loos & Dilworth, Inc. of Bristol, Pa., USA). Othersuitable hydrocarbon resins may be found in U.S. Pat. No. 5,667,902.

Preferred hydrocarbon resins include saturated alicyclic resins. Suchresins, if used, may have a softening point in the range of from about85° C. to about 140° C., or preferably in the range of about 100° C. toabout 140° C., as measured by the ring and ball technique. Examples ofsuitable, commercially available saturated alicyclic resins are ARKON—P®resins (commercially available from Arakawa Forest Chemical Industries,Ltd., of Japan).

The amount of the one or more hydrocarbon resins, either alone or incombination, in the film is preferably less than about 20 wt %, and morepreferably in the range of from about 1 wt % to about 5 wt %, based onthe total weight of the core layer.

Polypropylene

The term “polypropylene” as used herein broadly means any polymer thatis considered a “polypropylene” by persons skilled in the art (asreflected in at least one patent or publication), and includes homo,impact, and random polymers of propylene. Preferably, the polypropyleneused in the compositions described has a melting point above 110° C.,includes at least 90 wt % propylene units, and contains isotacticsequences of those units. The polypropylene can also include atacticsequences or syndiotactic sequences, or both. The polypropylene caneither derive exclusively from propylene monomers (i.e., having onlypropylene units) or derive from mainly propylene (more than 80%propylene) with the remainder derived from olefins, particularlyethylene, and/or C₄-C₁₀ alpha-olefins. The polypropylene can have a highMFR (e.g., from a low of 10, or 15, or 20 g/10 min to a high of 25 to 30g/10 min). The polypropylene can also have a lower MFR, e.g.,“fractional” polypropylenes which have an MFR less than 1.0. Those withhigh MFR are preferred for ease of processing or compounding.

In one or more embodiments, the polypropylene is or includes isotacticpolypropylene. Preferably, the polypropylene contains one or morecrystalline propylene homopolymers or copolymers of propylene having amelting temperature of from 110° C. to 170° C. or higher as measured byDSC. Preferred copolymers of propylene include, but are not limited to,terpolymers of propylene, impact copolymers of propylene, randompolypropylene and mixtures thereof. Preferred comonomers have 2 carbonatoms, or from 4 to 12 carbon atoms. Preferably, the comonomer isethylene. Such polypropylenes and methods for making the same aredescribed in U.S. Pat. No. 6,342,565.

The term “random polypropylene” as used herein broadly means a singlephase copolymer of propylene having up to 9 wt %, preferably 2 wt % to 8wt % of an alpha olefin comonomer. Preferred alpha olefin comonomershave 2 carbon atoms, or from 4 to 12 carbon atoms. Preferably, the alphaolefin comonomer is ethylene.

Thermoplastic Resin

The thermoplastic resin is or includes an olefinic thermoplastic resin.The “olefinic thermoplastic resin” can be any material that is not a“rubber” and that is a polymer or polymer blend considered by personsskilled in the art as being thermoplastic in nature, e.g., a polymerthat softens when exposed to heat and returns to its original conditionwhen cooled to room temperature. The olefinic thermoplastic resin cancontain one or more polyolefins, including polyolefin homopolymers andpolyolefin copolymers. Except as stated otherwise, the term “copolymer”means a polymer derived from two or more monomers (includingterpolymers, tetrapolymers, etc.), and the term “polymer” refers to anycarbon-containing compound having repeat units from one or moredifferent monomers.

Illustrative polyolefins can be prepared from mono-olefin monomersincluding, but not limited to, monomers having 2 to 7 carbon atoms, suchas ethylene, propylene, 1-butene, isobutylene, 1-pentene, 1-hexene,1-octene, 3-methyl-1-pentene, 4-methyl-1-pentene, 5-methyl-1-hexene,mixtures thereof and copolymers thereof with (meth)acrylates and/orvinyl acetates. Preferably, the olefinic thermoplastic resin isunvulcanized or non cross-linked. In embodiments where the film includespolypropylene, the thermoplastic resin is not a polypropylene.

Rubber

The rubber component can include one or more olefinic rubbers such asnon-polar, rubbery copolymers of two or more alpha-monoolefins,preferably copolymerized with at least one polyene, usually a diene.Saturated monoolefin copolymer rubber, for example, ethylene/propylenecopolymer rubber (EPM; about 45 to about 80% by weight of ethylene) orunsaturated monoolefin rubber such as ethylene/propylene/diene (EPDM;about 45 to about 80% by weight of ethylene, about 0.1 to about 15% byweight of non-conjugated diene, remainder being propylene) rubber can beused. EPDM is a terpolymer of ethylene, propylene and a non-conjugateddiene. Satisfactory non-conjugated dienes include5-ethylidene-2-norbornene (ENB); 1,4-hexadiene; 5-methylene-2-norbornene(MNB); 1,6-octadiene; 5-methyl-1,4-hexadiene;3,7-dimethyl-1,6-octadiene; 1,3-cyclopentadiene; 1,4-cyclohexadiene;dicyclopentadiene (DCPD) and vinyl norbornene (VNB).

Another olefinic rubber can include a C4-7 isomonoolefin and a para-C1-4alkylstyrene and, preferably, a halogenated derivative thereof. Theamount of halogen in the copolymer, predominantly in thepara-alkylstyrene, is from about 0.1 to 10 wt %. A preferred example isthe brominated copolymer of isobutylene and para-methylstyrene. Thesecopolymers are more fully described in U.S. Pat. No. 5,162,445, thedisclosure of which is fully incorporated herein by reference.

The rubber component can also include one or more styrenic blockcopolymers. Such block-copolymers can include styrene/conjugateddiene/styrene, with the conjugated diene optionally being fully orpartially hydrogenated, or mixtures thereof. Generally thisblock-copolymer can contain about 10 to about 50 wt %, more preferablyabout 25 to about 35 wt % of styrene and about 90 to about 50 wt %, morepreferably about 75 to about 65 wt % of the conjugated diene, based onsaid block-copolymer. Most preferably, however, is a block-copolymerwhich contains about 30 wt % of styrene and about 70 wt % of theconjugated diene. The conjugated diene can be selected from butadiene,isoprene or mixtures thereof. Specific block-copolymers of thestyrene/conjugated diene/styrene-type are SBS, SIS, SIBS, SEBS and SEPSblock-copolymers.

Butyl rubbers may also be used. The term “butyl rubber” includescopolymers of an isoolefin and a conjugated monoolefin, terpolymers ofan isoolefin with or without a conjugated monoolefin, divinyl aromaticmonomers and the halogenated derivatives of such copolymers andterpolymers. Useful butyl rubber copolymers include a major portion ofisoolefin and a minor amount, usually less than about 30 wt %, of aconjugated multi-olefin. The preferred copolymers include about 85 to99.5 wt % of a C4-7 isoolefin such as isobutylene and about 15 to 0.5 wt% of a multi-olefin of 4 to 14 carbon atoms, such as isoprene,butadiene, dimethyl butadiene and piperylene. Commercial butyl rubber,chlorobutyl rubber, and bromobutyl rubber, useful in the invention, arecopolymers of isobutylene and minor amounts of isoprene with less thanabout 3% halogen for the halobutyl-derivatives. Other butyl co- andterpolymer rubbers are illustrated by the description in U.S. Pat. No.4,916,180, the disclosure of which is fully incorporated herein byreference.

Natural rubber may also be used. The main constituent of natural rubberis the linear polymer cis-1,4-polyisoprene. It is normally commerciallyavailable in the form of smoked sheets and crepe. Synthetic polyisoprenemay also be used. Furthermore, polybutadiene rubber andstyrene-butadiene-copolymer rubbers may also be used.

In one or more embodiments, nitrite rubbers can be used. Examples of anitrite group-containing rubber include a copolymer rubber comprising anethylenically unsaturated nitrite compound and a conjugated diene.Further, the copolymer rubber can be one in which the conjugated dieneunits of the copolymer rubber are hydrogenated. Specific examples of theethylenically unsaturated nitrile compound include acrylonitrile,alpha-chloroacrylonitrile, alpha-fluoroacrylonitrile andmethacrylonitrile. Among them, acrylonitrile is preferred. Examples ofthe conjugated diene include 1,3-butadiene, 2-chlorobutadiene and2-methyl-1,3-butadiene (isoprene). Among them, butadiene is preferred.Preferred nitrite rubbers include copolymers of 1,3-butadiene and about10 to about 50 percent of acrylonitrile.

Slip Agents

In one or more embodiments, the polymer composition may include one ormore slip agents. Illustrative slip agents include fatty acids, higheraliphatic acid amides, higher aliphatic acid esters, waxes and metalsoaps. In one or more embodiments, the slip agents can include one ormore amides such as behenamide, erucamide, N-(2-hydroxyethyl) erucamide,lauramide, N,N′-ethylene bis-olamide, oleamide, oleyl palmitamide,stearyl erucamide, tallow amide, blends thereof, and combinationsthereof. In one or more embodiments, the slip agents are added to theblend in amounts ranging from about 0.1 to about 2 weight percent basedon the total weight of the blend.

Blending and Additives

In one or more embodiments, the one or more propylene-based polymers,thermoplastic resins, slip agents, and/or hydrocarbon resins can beblended by melt-mixing to form a blend. In one or more embodiments, theblend contains no processing oil. In other words, the blend is processedin the absence of processing oil. The blend may be prepared and mixedusing any appropriate method known to those having skill in the art, forexample, extruders with kneaders or mixing elements with one or moremixing tips or flights, extruders with one or more screws, extruders ofco or counter rotating type, Banbury mixers, Farrell Continuous mixers,or Buss Kneaders. The type and intensity of mixing, temperature, andresidence time required can be achieved by the choice of one of theabove machines in combination with the selection of kneading or mixingelements, screw design, and screw speed (typically <3000 RPM).

In one or more embodiments, the films described can be used as one ormore layers in a multi-film or laminate system. For example, an elasticlaminate having one or more facing layers disposed at least partiallyabout one or more inner layers is provided. In one or more embodiments,the one or more facing layers may include at least 60 wt %, at least 70wt %, at least 80 wt %, at least 90 wt %, or at least 95 wt % of thepropylene-based polymer.

In one or more embodiments, the facing layer can include thepropylene-based polymer in an amount ranging from a low of about 60, 70,or 75 wt % to a high of about 80, 90, 95 wt %. In one or moreembodiments, the facing layer can include polypropylene in an amountranging from a low of about 5, 10 or 20 wt % to a high of about 25, 30,or 40 wt %. In one or more embodiments, the facing layer can include oneor more thermoplastic resins in an amount ranging from a low of about 5,10 or 20 wt % to a high of about 25, 30, or 40 wt %.

In one or more embodiments, the facing layer may include about 70 wt %to about 95 wt % of the propylene-based polymer and about 5 wt % toabout 30 wt % of polypropylene. In one or more embodiments, the facinglayer may include about 65 wt % to about 80 wt % of the propylene-basedpolymer and about 20 wt % to about 35 wt % of polypropylene. When theone or more thermoplastic resins are present, the facing layer blend mayinclude about 60 wt % to about 95 wt % of the propylene-based polymerand about 5 wt % to about 40 wt % of polypropylene.

In one or more embodiments, the one or more inner layers may include atleast 60 wt %, at least 70 wt %, at least 80 wt %, at least 90 wt %, orat least 95 wt % of the propylene-based polymer.

In one or more embodiments, the one or more inner layers may includefrom about 2 to about 30 wt % of the one or more slip agents. In one ormore embodiments, the one or more inner layers may include from about0.2 wt % to about 20 wt % of the one or more slip agents. In one or moreembodiments, the one or more inner layers may include from about 0.2 wt% to about 10 wt % of the one or more slip agents. In one or moreembodiments, the one or more inner layers may include from about 0.2 wt% to about 5 wt % of the one or more slip agents. In one or moreembodiments, the one or more inner layers may include the one or moreslip agents in an amount ranging from a low of about 0.2 wt %, 0.5 wt %or 1 wt % to a high of about 2 wt %, 5 wt % or 10 wt %.

In one or more embodiments, the one or more inner layers may includefrom about 2 to about 30 wt % of the one or more hydrocarbon resins. Inone or more embodiments, the one or more inner layers may include fromabout 0.2 wt % to about 20 wt % of the one or more hydrocarbon resins.In one or more embodiments, the one or more inner layers may includefrom about 0.2 wt % to about 10 wt % of the one or more hydrocarbonresins. In one or more embodiments, the one or more inner layers mayinclude from about 0.2 wt % to about 5 wt % of the one or morehydrocarbon resins. In one or more embodiments, the one or more innerlayers include the one or more hydrocarbon resins in an amount rangingfrom a low of about 0.2 wt %, 0.5 wt % or 1 wt % to a high of about 2 wt%, 5 wt % or 10 wt %.

In one or more embodiments, the inner layer or facing layer may containadditional additives, which can be introduced at the same time as theother components, or later downstream in case of using an extruder orBuss kneader, or merely later in time. Examples of such additives areantioxidants, antiblocking agents, antistatic agents, ultravioletstabilizers, foaming agents, and processing aids. Such additives mayinclude from about 0.1 to about 10 percent by weight based on the totalweight of blend. The additives can be added to the blend by any methodacceptable to persons skilled in the art, for example in pure form or inmaster batches.

Articles

The polymer composition described may be used to form a variety ofarticles, including but not limited to consumer and industrial goods.Illustrative consumer articles include but are not limited toincontinence pads, personal hygiene articles, disposable diapers,training pants, clothing, undergarments, sports apparel, face masks,gowns, and filtration media. The terms “nonwoven, “nonwoven fabric,” and“nonwoven web,” as used herein, are used interchangeably and refer to aweb or fabric that has a structure of individual fibers or filamentsthat are randomly interlaid, but not in an identifiable repeatingpattern.

The terms “elastic” and “semi-elastic” refer to any material having atension set of 80% or less, or 60% or less, or 50% or less, or 25% orless at 100% elongation and at a temperature between the glasstransition temperature and the crystalline melting point. Elasticpolymer materials and compositions are also referred to in the art as“elastomers” and/or “elastomeric.”

Preferably, a nonwoven fabric is layered with one or more facing layersthermally bonded to one or more inner layers. Each layer may be eitherspunbonded or meltblown to from a single fabric layer. Accordingly, thelayered nonwoven fabric can include numerous combinations of spunbonded(S) and meltblown (M) layers including but not limited tospunbond-spunbond (SS), spunbond-meltblown-spunbond (SMS),spunbond-spunbond-spunbond (SSS), spunbond-meltblown-meltblown-spunbond(SMMS) spunbond-spunbond-spunbond-spunbond (SS-SS), spunbond-meltblownor vice versa (SM or MS),spunbond-meltblown-spunbond-spunbond-meltblown-spunbond (SMS-SMS),spunbond-meltblown-meltblown-spunbond-spunbond-meltblown-meltblown-spunbond(SMMS-SMMS) arrangements, as well as many other combinations andvariations of the foregoing. The multiple fabric layers are then bondedtogether by the application of heat and pressure to form the desiredfabric composite. The spunbonded fabric layers may be prebonded byheated press rolls to provide structural integrity to the fabric.

As mentioned above, the one or more facing layers may be thermallybonded to the one or more inner layers. The layers can be thermallybonded using a calendering process or any other process known in theart. It is believed that the inner layer(s) containing one or more slipagents and/or one or more hydrocarbon resins eliminates the “rubberyfeel” that is intrinsic to an unmodified elastic nonwoven. As such, themodified elastic nonwoven has an appealing touch to the wearer.

As used herein, the terms “thermal bonding” and “thermally bonded” referto the heating of fibers to effect the melting (or softening) and fusingof fibers such that a nonwoven fabric is produced. Thermal bondingincludes calendar bonding and through-air bonding, as well as othermethods known in the art.

Considering fabrics in more detail, melt blown fabrics are generallywebs of fine filaments having a fiber diameter in the range of fromabout 0.1 to about 20 microns. Typical fiber diameters for melt blownfabrics are in the range of from 1 to 10 microns, or from 1 to 5microns. The nonwoven webs formed by these fine fiber diameters havevery small pore sizes and can, therefore, have excellent barrierproperties.

The meltblown layers may be prepared by extruding the blend in moltenform through a plurality of fine, usually circular capillaries of a die.A high-velocity, usually heated gas (e.g., air) stream attenuates thefilaments of molten thermoplastic material to reduce their diameter.Thereafter the meltblown fibers, which include any melt processableadditives that were present in the blend, are carried by thehigh-velocity heated gas stream and are deposited on a collectingsurface to form a nonwoven web of randomly dispersed meltblown fibers.

The spunbonded layers may be produced by continuously extruding theblend through a plurality of fine, usually circular capillaries of aspinnerette having typically 1000 holes per meter length, or with banksof smaller spinnerets, with each spinneret section containing as few as40 holes. After exiting the spinneret, the molten fibers are quenched bya cross-flow air quench system, then pulled away from the spinneret andattenuated (drawn) by high speed air. The friction between the flowingair and the filaments creates a force which draws the filaments, i.e.,attenuates the filaments to a smaller diameter. The filaments are drawnto achieve molecular orientation and tenacity. The continuous filamentsare then deposited in a substantially random manner to form a web ofsubstantially continuous and randomly arranged, molecularly orientedfilaments. The web is then passed through compaction rolls and thenbetween heated calender rolls where the raised lands on one roll bondthe web at points covering 10% to 40% of its area to form a nonwovenfabric. The top calender roll may have an embossed pattern while thebottom roll is typically smooth.

In one or more embodiments, any one of the one or more facing layers andthe one or more inner layers may be a multicomponent layer. The term“multicomponent” as used herein, refers to fibers which have been formedfrom at least two polymers extruded from separate extruders andmeltblown or spun together to form one fiber. Multicomponent fibers arealso referred to in the art as bicomponent fibers. The polymers used inmulticomponent fibers are typically different from each other; however,conjugated fibers can be monocomponent fibers. The polymers can bearranged in distinct zones across the cross-section of the conjugatedfibers and extend continuously along the length of the conjugatedfibers. The configuration of conjugated fibers can be, for example, asheath/inner arrangement wherein one polymer is surrounded by another, aside by side arrangement, a pie arrangement or an “islands-in-the-sea”arrangement. Conjugated fibers are described in U.S. Pat. Nos.5,108,820; 5,336,552; and 5,382,400; the entire disclosures of which arehereby incorporated herein by reference. In some embodiments, the fibersdescribed herein may be part of a conjugated configuration.

In one or more embodiments, the fibers may be in the form of continuousfilament yarn, partially oriented yarn, and/or staple fibers. Continuousfilament yarns typically range from 40 denier to 20,000 denier(denier=number of grams per 9000 yards). Filaments generally range from1 to 20 or more denier per filament (dpf). Spinning speeds are typically800 m/min to 1500 m/min (2500 ft/min to 5000 ft/min).

Partially oriented yarn (POY) is the fiber produced directly from fiberspinning without solid state drawing, as in the continuous filament. Theorientation of the molecules in the fiber is done in the melt state justafter the molten polymer leaves the spinneret.

Staple fiber filaments can range, for example, from 1.5 dpf to 70 dpf ormore, depending on the application. There are two basic staple fiberfabrication processes: traditional and compact spinning. The traditionalprocess typically involves two steps: 1) producing, applying, finishing,and winding, followed by 2) drawing, a secondary finish application,crimping, and cutting into the staple. During the traditional spinningprocess, a ‘triangle’ is created as fibers are drawn out of anapparatus. Compact spinning minimizes or eliminates the triangle, andmay reduce the amount of stray fibers and weak spots in a thread. It iscalled ‘compact’ because outside fibers are compacted towards the coreof the yarn as they are twisted.

In some embodiments, the fabrics can be further processed. For example,the fabric can be subjected to a surface treatment process, such assizing. Thus, in some embodiments, the fabric can contain sizingadditives such as rosins, resins, or waxes. As another example, thefabric can be subjected to a tentering process. In one or moreembodiments above, blocking agents can be added to the fabric in aprocessing step subsequent to the formation of the fabric.

Definitions and Test Methods

For purposes of convenience, various definitions and specific testprocedures are identified below. However, if a person of ordinary skillwishes to determine whether a composition or polymer has a particularproperty identified in a claim herein, then any published orwell-recognized method or test procedure can be followed to determinethat property, although the specifically identified procedure ispreferred. Each claim should be construed to cover the results of any ofsuch procedures, even to the extent different procedures may yielddifferent results or measurements. Thus, a person of ordinary skill inthe art is to expect experimental variations in measured properties thatare reflected in the claims. All numerical values can be considered tobe “about” or “approximately” the stated value, in view of the nature oftesting in general.

Comonomer content: The comonomer content and sequence distribution ofthe polymers can be measured using ¹³C nuclear magnetic resonance (NMR)by methods well known to those skilled in the art. Comonomer content ofdiscrete molecular weight ranges can be measured using methods wellknown to those skilled in the art, including Fourier Transform InfraredSpectroscopy (FTIR) in conjunction with gel permeation chromatography(GPC), as described in Wheeler and Willis, Applied Spectroscopy, 1993,Vol. 47, pp. 1128-1130.

In the particular case of propylene-ethylene copolymers containinggreater than 75 wt % propylene, the comonomer content may be measured asfollows. A thin homogeneous film is pressed at a temperature of about150° C. or greater, and mounted on a Perkin Elmer PE 1760 infraredspectrophotometer. A full spectrum of the sample from 600 cm⁻¹ to 4000cm⁻¹ is recorded and the monomer weight percent of ethylene can becalculated according to the following equation: Ethylene wt%=82.585−111.987X+30.045X², where X is the ratio of the peak height at1155 cm⁻¹ and peak height at either 722 cm⁻¹ or 732 cm⁻¹, whichever ishigher.

Polyene content: The amount of polyene present in a polymer may beinferred by the quantitative measure of the amount of the pendant freeolefin present in the polymer after polymerization. Several proceduressuch as iodine number and the determination of the olefin content by H¹or ¹³C nuclear magnetic resonance (NMR) have been established. Inembodiments described herein where the polyene is ENB, the amount ofpolyene present in the polymer can be measured using ASTM D-3900.

Isotactic: The term “isotactic” is defined herein as a polymer sequencein which greater than 50% of the pairs of pendant methyl groups locatedon adjacent propylene units, which are inserted into the chain in aregio regular 1,2 fashion and are not part of the backbone structure,are located either above or below the atoms in the backbone chain, whensuch atoms in the backbone chain are all in one plane. Certaincombinations of polymers in blends or polymer sequences within a singlepolymer are described as having “substantially the same tacticity,”which herein means that the two polymers are both isotactic according tothe definition above.

Tacticity: The term “tacticity” refers to the stereoregularity of theorientation of the methyl residues from propylene in a polymer. Pairs ofmethyl residues from contiguous propylene units identically insertedwhich have the same orientation with respect to the polymer backbone aretermed “meso” (m). Those of opposite configuration are termed “racemic”(r). When three adjacent propylene groups have methyl groups with thesame orientation, the tacticity of the triad is ‘mm’. If two adjacentmonomers in a three monomer sequence have the same orientation, and thatorientation is different from the relative configuration of the thirdunit, the tacticity of the triad is ‘mr’. When the middle monomer unithas an opposite configuration from either neighbor, the triad has ‘rr’tacticity. The fraction of each type of triad in the polymer can bedetermined and when multiplied by 100 indicates the percentage of thattype found in the polymer.

The triad tacticity of the polymers described herein can be determinedfrom a ¹³C nuclear magnetic resonance (NMR) spectrum of the polymer asdescribed below and as described in U.S. Pat. No. 5,504,172, thedisclosure of which is hereby incorporated herein by reference.

Tacticity Index: The tacticity index, expressed herein as “m/r”, isdetermined by ¹³C nuclear magnetic resonance (NMR). The tacticity indexm/r is calculated as defined in H. N. Cheng, Macromolecules, pg. 17,1950 (1984). An m/r ratio of 1.0 generally describes a syndiotacticpolymer, and an m/r ratio of 2.0 generally describes an atacticmaterial. An isotactic material theoretically can have a ratioapproaching infinity, and many by-product atactic polymers havesufficient isotactic content to result in ratios of greater than 50.

Melting point and heat of fusion: The melting point (Tm) and heat offusion of the polymers described herein can be determined byDifferential Scanning Calorimetry (DSC), using the ASTM E-794-95procedure. About 6 to 10 mg of a sheet of the polymer which has beenpressed at approximately 200° C. to 230° C. is removed with a punch dieand annealed at room temperature for 48 hours. At the end of thisperiod, the sample is placed in a Differential Scanning Calorimeter(Perkin Elmer Pyris One Analysis System and cooled to about −50° C. to−70° C. The sample is heated at about 20° C./min to attain a finaltemperature of about 180° C. to 200° C. The term “melting point,” asused herein, is the highest peak among principal and secondary meltingpeaks as determined by DSC, discussed above. The thermal output isrecorded as the area under the melting peak of the sample, which istypically at a maximum peak at about 30° C. to about 175° C. and occursbetween the temperatures of about 0° C. and about 200° C. The thermaloutput is measured in Joules as a measure of the heat of fusion. Themelting point is recorded as the temperature of the greatest heatabsorption within the range of melting of the sample.

Molecular weight and molecular weight distribution: The molecular weightand molecular weight distribution of the polymers described herein canbe measured as follows. Molecular weight distribution (MWD) is a measureof the range of molecular weights within a given polymer sample. It iswell known that the breadth of the MWD can be characterized by theratios of various molecular weight averages, such as the ratio of theweight average molecular weight to the number average molecular weight,Mw/Mn, or the ratio of the Z-average molecular weight to the weightaverage molecular weight Mz/Mw.

Mz, Mw, and Mn can be measured using gel permeation chromatography(GPC), also known as size exclusion chromatography (SEC). This techniqueutilizes an instrument containing columns packed with porous beads, anelution solvent, and detector in order to separate polymer molecules ofdifferent sizes. In a typical measurement, the GPC instrument used is aWaters chromatograph equipped with ultrastyro gel columns operated at145° C. The elution solvent used is trichlorobenzene. The columns arecalibrated using sixteen polystyrene standards of precisely knownmolecular weights. A correlation of polystyrene retention volumeobtained from the standards, to the retention volume of the polymertested yields the polymer molecular weight.

Average molecular weights M can be computed from the expression:

$M = \frac{\sum\limits_{i}{N_{i}M_{i}^{n + 1}}}{\sum\limits_{i}{N_{i}M_{i}^{n}}}$

where Ni is the number of molecules having a molecular weight Mi. Whenn=0, M is the number average molecular weight Mn. When n=1, M is theweight average molecular weight Mw. When n=2, M is the Z-averagemolecular weight Mz. The desired MWD function (e.g., Mw/Mn or Mz/Mw) isthe ratio of the corresponding M values. Measurement of M and MWD iswell known in the art and is discussed in more detail in, for example,Slade, P. E. Ed., Polymer Molecular Weights Part II, Marcel Dekker,Inc., NY, (1975) pp. 287-368; Rodriguez, F., Principles of PolymerSystems 3^(rd) ed., Hemisphere Pub. Corp., NY, (1989) pp. 155-160; U.S.Pat. No. 4,540,753; Verstrate et al., Macromolecules, Vol. 21, (1988)pg. 3360; and references cited therein.

Mooney viscosity: Mooney viscosity, as used herein, is measured asML(1+4) @ 125° C. according to ASTM D-1646.

Melt flow rate and melt index: The determination of the Melt Flow Rate(MFR) and the Melt Index (MI) of the polymer is made according to ASTMD-1238 using modification 1 with a load of 2.16 kg. In this version ofthe method, a portion of the sample extruded during the test iscollected and weighed. The sample analysis is conducted at 230° C. witha 1 minute preheat on the sample to provide a steady temperature for theduration of the experiment. This data, expressed as dg of sampleextruded per minute, is indicated as MFR. In an alternative procedure,the test is conducted in an identical fashion except at a temperature of190° C. This data is referred to as MI@190° C.

Isotacticity Index: The isotacticity index is calculated according tothe procedure described in EP 0 374 695A2. The IR spectra of a thin filmof the material is recorded and the absorbance at 997 cm⁻¹ and theabsorbance at 973 cm⁻¹ are determined. The quotient of the absorbance at997 cm⁻¹ to the absorbance at 973 cm⁻¹ is multiplied by 100 to yield theisotacticity index. In the determination of the absorbance at these twopositions, the position of zero absorbance is the absorbance when thereis no analytical sample present in the sample beam.

EXAMPLES

The foregoing discussion may be further described with reference to thefollowing non-limiting examples. The examples illustrate the advantagesand effects of films having one or more hydrocarbon resins added to oneor more propylene-based polymers. The examples formulated according toone or more embodiments described provided films with significantlyimproved tear properties with minimal to no loss in elastic properties.The most notable improved tear properties was intrinsic tear. Such filmswere nothing short of surprising and unexpected.

The samples were compression molded per ASTM D 4703-03 to 4-6 mil.Hysteresis tests were run on compression molded specimens in a tensiletester to an extension of 100% or 300% and returned to zero load. Thetests were performed at a cross head speed of 508 mm/min. The testcondition corresponding to the first cycle is designated “as is,” andthe second cycle is designated as “pre stretch.” The pre stretch testconditions also correspond to 100% or 300% extension and return to zeroload. Permanent set and load loss properties as defined below werecalculated for both “as is” and “pre stretch” conditions.

Permanent Set (%): Strain level corresponding to zero force on return,upon stretching a non woven fabric to 100% extension. This can be doneeither in the machine direction or the transverse direction.

Load Loss (%): (Load on Ascending Curve−Load on Descending Curve)/Loadon Ascending calculated at the 50% strain level.

Hysteresis (lb-in/in): Area enclosed by the ascending and descendingportion of the load displacement curve.

Mechanical Hysteresis (lb-in/in): Area under the ascending portion ofthe load displacement curve.

Hysteresis (%): Hysteresis/Mechanical Hysteresis.

PS: Pre stretch to 100% strain.

Intrinsic tear was measured according ASTM D-1922-03.

Tensile tests were performed according to ASTM D-638

Example 1

Table 1 shows blend examples comprising a propylene based polymerdesignated Copolymer A (available from ExxonMobil Chemical Company), astyrenic block copolymer (D4211) and hydrocarbon resin based polymeradditive (PR 100A), compounded in a 30 mm ZSK twin screw extruder. Theingredients were tumble blended to a total weight of 5000 gm, andintroduced into the hopper of the twin screw extruder. The melttemperature was maintained at 210° C. The extrudate was cooled in awater trough and pelletized for testing.

Example C1 is a comparative example based on Copolymer A that was notcompounded, and directly converted to test specimens. Example 2 shows arecipe containing 15 wt. % PR 100A. As seen in Table 1, the intrinsictear properties were substantially enhanced from 1.6 gm/micron for C1 to3.9 gm/micron for Example 2. Both permanent set and load loss remainedessentially unchanged. Copolymer A is a propylene-based polymercontaining about 16 wt % ethylene, 3 g/10 min MFR, and a heat of fusionof about 5 J/g.

Example 3 contained D4211 as a third ingredient. This example exhibiteda substantial increase in intrinsic tear relative to C1 (2.6 gm/micron)without compromising the elastic properties.

TABLE 1 Properties of Copolymer A films modified with PR 100A EXAMPLE C12 3 Copolymer A 100.0 85.0 70.0 D4211 (14.3 MFR, 0.936 d) 0.0 0.0 21.5PR 100A 0.0 15.0 8.5 Irganox 1010 0.5 0.5 0.5 Total 100.5 100.5 100.5Compression Molded to 9 mil (0.23 mm) thickness MFR (230° C., 2.16 Kg)g/10 min 3.0 4.7 5.5 Tensile @ Yield¹ MPa 0.9 0.1 0.7 Tensile @ Brk MPa12.2 9.4 10.0 Elongation @ Yield % 10 10 10 Elongation @ Brk % 757 856805 Intrinsic Tear (Average thickness = g/micron 1.6 3.9 2.6 0.102 mm)Hysterisis As Is (100% Stretch) Set % 19 12 20 Load Loss @ 50% strain %44 45 21 Hysterisis Prestretch to 100% and 100% Stretch Set % 18 19 19Load Loss @ 50% strain % 38 44 46 Hysterisis As Is (300% Stretch) Set %50 50 50 Load Loss @ 150% strain % 57 57 57 Hysterisis Prestretch to300% and 300% Stretch Set % 46 46 46 Load Loss @ 150% strain % 44 44 44¹Thickness: 0.31 mm, Speed 508 mm/mm, Width 25.4 mm, Length 102 mm)

Example 2

Table 2 shows examples of Copolymer A blended with hydrocarbon resinbased additives PR 103J or PR 100A in a laboratory PRISM extruder. Abatch weight of 500 gm, wherein the ingredients were homogenized thoughtumble blending, was selected for all the examples. Extrusioncompounding was completed at a melt temperature of 210° C., and theextrudates were collected as a solid mass in a cardboard boatspray-coated with silicone to facilitate release. The compound wasreduced to smaller fragments in a guillotine and compression molded intotest specimens.

From Table 2, it is evident that the addition of PR 103J atprogressively increasing levels (Examples 5 through 7) enhancedintrinsic tear properties relative to the comparative example C4,without affecting elastic properties. A similar trend was observed withPR 100A, although in this case about 10 wt. % (Example 9) appears tohave provided the optimal enhancement. Surprisingly, a further increasebeyond this level resulted in a marginal loss of tear properties asevidenced in Examples 10 and 11. The elastic properties of examples 9through 11 were similar or in some cases marginally better than thecomparative C4. In particular, the permanent set at 300% extension wasaround 33% in Examples 9 through 11 compared to 42% in comparative C4.

TABLE 2 Copolymer A films modified with mixtures of PR additives EXAMPLEC4 5 6 7 8 9 10 11 Copolymer A 100.0 90.0 85.0 80.0 80.0 90.0 85.0 80.0PR 103J 0.0 10.0 15.0 20.0 20.0 0.0 0.0 0.0 PR 100A 0.0 0.0 0.0 0.0 8.510.0 15.0 20.0 Irganox 1010 0.0 0.5 0.5 0.5 0.5 0.5 0.5 0.5 Total 100.0100.5 100.5 100.5 109.0 100.5 100.5 100.5 Compression Mold to 9 mil(0.23 mm) thickness Hardness Shore A 46.0 42.0 39.0 40.0 35.0 42.0 40.040.0 1% Secant Modulus MPa 9.5 8.2 6.5 4.6 8.7 9.9 7.0 7.0 TangentModulus MPa 11.6 7.6 7.1 5.2 5.7 7.1 6.6 6.7 Intrinsic Tear (Average =0.102 mm) gm/micron 1.3 1.5 1.8 2.6 3.9 3.7 2.5 3.2 Hysterisis As Is(100% Stretch) Set % 7 7 8 8 8 8 8 7 Load Loss @ 50% strain % 38 36 3737 36 38 37 38 Hysterisis Prestretch to 100% and 100% Stretch Set % 6 67 8 7 7 7 5 Load Loss @ 50% strain % 26 27 26 29 28 27 27 28 HysterisisAs Is (300% Stretch) Set % 42 34 32 33 32 33 32 33 Load Loss @ 150%strain % 59 57 56 54 55 57 56 56 Hysterisis Prestretch to 300% and 300%Stretch Set % 34 28 29 31 30 28 29 29 Load Loss @ 150% strain % 45 41 4242 42 43 43 42

Example 3

Table 3 shows examples 13-19 containing propylene based polymersCopolymer B or Copolymer C with styrenic block polymer D4211 and PR 103Jpolymer additive. Copolymer B is a propylene-based polymer containingabout 15 wt % ethylene, 3 g/10 min MFR, and a heat of fusion of about 5J/g. Copolymer C is a propylene-based polymer containing about 14 wt %ethylene, 20 g/10 min MFR, and a heat of fusion of about 10 J/g.

Examples 13-19 were prepared in a 30 mm ZSK twin screw extruder asoutlined in Example 1. The comparative examples C12 and C16 were 70/30blends of Copolymer B and Copolymer C. D4211 was added in Examples 13and 14. PR 103J was added at the expense of Copolymer B by maintainingthe D4211 resin level at 30 wt %. In Example 15, the D4211 was droppedto 20 wt %. Examples 17 through 19 illustrated a similar trend withCopolymer C (20 MFR) as the base resin instead of Copolymer B. Examples13 through 15 displayed higher tear properties compared to comparativeexample C12 with a comparable or marginal decrease in elasticproperties. Similarly, Examples 17 through 19 exhibited higher tearproperties compared to comparative example C16 while maintaining elasticproperties.

TABLE 3 Properties of copolymer films modified with PP 103J C12 13 14 15C16 17 18 19 Copolymer B 70 60 55 65 0 0 0 0 Copolymer C 0 0 0 0 70 6055 65 D4211 30 30 30 15 30 30 30 15 PR1O3J 0 10 15 20 0 10 15 20 Irganox1010 0.5 0.5 0.5 0.5 0.5 0.5 0.5 0.5 Total 100.5 100.5 100.5 100.5 100.5100.5 100.5 100.5 Compression Mold to 9 mil (0.23 mm) thickness MFR(230° C., 2.16 Kg) g/10 min 6.6 9.3 17.7 16.8 22.1 35.2 39.3 41.3Tensile @ Yield MPa 1.0 0.8 0.7 0.6 1.0 0.7 0.7 0.7 Tensile @ Brk MPa19.9 18.7 17.4 10.5 10.7 10.1 9.2 8.3 Elongation@Yield % 10 11 12 11 1110 8 13 Elongation@ Brk % 985 1002 1058 906 992 1080 1137 1111 IntrinsicTear (Average = 0.10 mm) 2.1 2.5 3.1 5.4 1.6 2.2 3.1 4.4 gm/micronHysterisis (300% Stretch) Set % 50 50 50 53 48 50 52 53 Load Loss @ 150%strain % 57 56 52 59 60 56 54 61 Hysterisis (300% Stretch) Set % 46 4649 54 48 48 53 55 Load Loss @ 150% strain % 44 41 41 46 44 41 44 51

Specific embodiments of the invention are further described in thefollowing pararaphs:

1. A film comprising:

one or more propylene-based polymers having (i) 60 wt % or more unitsderived from propylene, (ii) isotactically arranged propylene derivedsequences, and (iii) a heat of fusion less than 65 J/g; and

one or more hydrocarbon resins each having a glass transitiontemperature greater than 20° C.

2. The film according to paragraph 1, wherein the amount of thehydrocarbon resin in the composition is sufficient to increase intrinsictear of the film by at least 20%.3. The film of paragraph 1 or 2, wherein the one or more propylene-basedpolymers has a heat of fusion less than 45 J/g4. The film according to any of paragraphs 1 to 3, wherein the one ormore propylene-based polymers has an ethylene content of from 5 wt % to16 wt %.5. The film according to any of paragraphs 1 to 4, wherein the one ormore propylene-based polymers has an ethylene content of from 12 wt % to16 wt %.6. The film according to any of paragraphs 1 to 5, wherein the one ormore propylene-based polymers has an ethylene content of from 15 wt % to16 wt %.7. The film according to any of paragraphs 1 to 6, wherein the one ormore propylene-based polymers has a melt flow rate (230° C./2.16 Kg) ofabout 1 g/10 min to about 400 g/10 min.8. The film according to any of paragraphs 1 to 7, wherein the one ormore propylene-based polymers has a melt flow rate (230° C./2.16 Kg) ofabout 1 g/10 min to about 30 g/10 min.9. The film according to any of paragraphs 1 to 8, wherein thepropylene-based polymer has a melt flow rate (230° C./2.16 Kg) of atleast 3.0 g/10 min.10. The film according to any of paragraphs 1 to 9, wherein thepropylene-based polymer has a melt flow rate (230° C./2.16 Kg) of atleast 20 g/10 min.11. The film according to any of paragraphs 1 to 10, wherein thepropylene-based polymer has a density of at least 0.80 g/cm³.12. The film according to any of paragraphs 1 to 11, wherein thepropylene-based polymer has a density of about 0.85 g/cm³ or more.13. The film according to any of paragraphs 1 to 12, wherein thepropylene-based polymer has a density of about 0.86 g/cm³ or more.14. The film according to any of paragraphs 1 to 13, wherein thepropylene-based polymer has a melt temperature of less than 110° C.15. The film according to any of paragraphs 1 to 14, wherein thehydrocarbon resin is a hydrogenated cycloaliphatic resin.16. The film according to any of paragraphs 1 to 15, wherein thehydrocarbon resin has a molecular weight (Mn) of from 200 to 5000.17. The film according to any of paragraphs 1 to 16, wherein thehydrocarbon resin has a molecular weight (Mn) of from 200 to 1000.18. The film according to any of paragraphs 1 to 17, wherein thehydrocarbon resin has a molecular weight (Mn) of from 500 to 1000.19. The film according to any of paragraphs 1 to 18, wherein thehydrocarbon resin has a softening point of from 80° C. to 180° C.20. The film according to any of paragraphs 1 to 19, wherein thehydrocarbon resin has a softening point of from 120° C. to 150° C.21. The film according to any of paragraphs 1 to 20, wherein thehydrocarbon resin has a softening point of from 125° C. to 140° C.22. A method for making a film composition, comprising:

admixing one or more propylene-based polymers and one or more misciblehydrocarbon resins in an amount sufficient to provide a film having anincrease in intrinsic tear by at least 5% compared to a film withouteither the one or more propylene-based polymers or the one or moremiscible hydrocarbon resins,

the propylene-based polymers each having (i) 60 wt % or more unitsderived from propylene, (ii) isotactically arranged propylene derivedsequences, and (iii) a heat of fusion less than 45 J/g; and thehydrocarbon resins each having a glass transition temperature greaterthan 20° C.

23. The method according to paragraph 22, further comprisingpolypropylene or one or more thermoplastic resins.24. The method according to paragraphs 22 or 23, wherein thepropylene-based polymer is present in the film in an amount of from 80to 99 wt % and the hydrocarbon resin is present in an amount of from 1to 20 wt %, based on the total weight of the film.25. The method according to any of paragraphs 22 to 24, wherein thepropylene-based polymer is present in the composition in an amount offrom 80 to 95 wt % and the hydrocarbon resin is present in an amount offrom 5 to 20 wt %, based on the total weight of the composition.26. The method according to any of paragraphs 22 to 25, wherein theintrinsic tear of the film is at least 1.5 gm/micron.27. The method according to any of paragraphs 22 to 26, wherein theintrinsic tear of the film is at least 2.6 gm/micron.28. The method according to any of paragraphs 22 to 27, wherein theintrinsic tear of the film is at least 3.9 gm/micron.29. The method according to any of paragraphs 22 to 28, furthercomprising one or more styrenic block copolymers.30. The method according to any of paragraphs 22 to 29, wherein thepropylene-based polymer has a melt flow rate (230° C./2.16 Kg) of atleast 3.0 g/10 min.31. The method according to any of paragraphs 22 to 30, wherein thepropylene-based polymer has a melt flow rate (230° C./2.16 Kg) of atleast 20 g/10 min.32. The method according to any of paragraphs 22 to 31, wherein thepropylene-based polymer has a density of at least 0.80 g/cm³.33. The method according to any of paragraphs 22 to 32, wherein thepropylene-based polymer has a density of about 0.85 g/cm³ or more.34. The method according to any of paragraphs 22 to 33, wherein thepropylene-based polymer has a density of about 0.86 g/cm³ or more.35. The method according to any of paragraphs 22 to 34, wherein thepropylene-based polymer has a melt temperature of less than 110° C.36. The method according to any of paragraphs 22 to 35, wherein thehydrocarbon resin is a hydrogenated cycloaliphatic resin.37. The method according to any of paragraphs 22 to 36, wherein thehydrocarbon resin has a molecular weight (Mn) of from 200 to 5000.38. The method according to any of paragraphs 22 to 37, wherein thehydrocarbon resin has a molecular weight (Mn) of from 200 to 1000.39. The method according to any of paragraphs 22 to 38, wherein thehydrocarbon resin has a molecular weight (Mn) of from 500 to 1000.40. The method according to any of paragraphs 22 to 39, wherein thehydrocarbon resin has a softening point of from 80° C. to 180° C.41. The method according to any of paragraphs 22 to 40, wherein thehydrocarbon resin has a softening point of from 120° C. to 150° C.42. The method according to any of paragraphs 22 to 41, wherein thehydrocarbon resin has a softening point of from 125° C. to 140° C.43. A film comprising:

one or more propylene-based polymers having 60 wt % or more unitsderived from propylene, isotactically arranged propylene derivedsequences, a heat of fusion less than 45 J/g, a density of at least 0.80g/cm³, and a MFR of at least 3.0 g/10 min; and

one or more hydrogenated cycloaliphatic resin each having a molecularweight (Mn) of from 200 to 5,000 and a glass transition temperaturegreater than 20° C., wherein the amount of the hydrocarbon resin in thecomposition is sufficient to increase intrinsic tear of the film by atleast 5%.

44. The film according to paragraph 43, wherein the hydrocarbon resinhas a softening point of from 125° C. to 140° C.45. The film according to paragraphs 43 or 44, wherein the intrinsictear of the film is at least 3.9 gm/micron.46. The film according to any of paragraphs 43 to 45, wherein the filmis a blown film.47. The film according to any of paragraphs 43 to 46, wherein the filmis a blown film.48. The film according to any of paragraphs 43 to 47, further comprisingpolypropylene or one or more thermoplastic resins.49. The film according to any of paragraphs 43 to 48, wherein thepropylene-based polymer is present in the film in an amount of from 80to 99 wt % and the hydrocarbon resin is present in an amount of from 1to 20 wt %, based on the total weight of the film.50. The film according to any of paragraphs 43 to 49, wherein thepropylene-based polymer is present in the composition in an amount offrom 80 to 95 wt % and the hydrocarbon resin is present in an amount offrom 5 to 20 wt %, based on the total weight of the composition.51. The film according to any of paragraphs 43 to 50, wherein theintrinsic tear of the film is at least 1.5 gm/micron.52. The film according to any of paragraphs 43 to 51, wherein theintrinsic tear of the film is at least 2.6 gm/micron.53. The film according to any of paragraphs 43 to 52, wherein theintrinsic tear of the film is at least 3.9 gm/micron.54. The film according to any of paragraphs 43 to 53, further comprisingone or more styrenic block copolymers.

Certain embodiments and features have been described using a set ofnumerical upper limits and a set of numerical lower limits. It should beappreciated that ranges from any lower limit to any upper limit arecontemplated unless otherwise indicated. Certain lower limits, upperlimits and ranges appear in one or more claims below. All numericalvalues are “about” or “approximately” the indicated value, and take intoaccount experimental error and variations that would be expected by aperson having ordinary skill in the art.

Various terms have been defined above. To the extent a term used in aclaim is not defined above, it should be given the broadest definitionpersons in the pertinent art have given that term as reflected in atleast one printed publication or issued patent. Furthermore, allpatents, test procedures, and other documents cited in this applicationare fully incorporated by reference to the extent such disclosure is notinconsistent with this application and for all jurisdictions in whichsuch incorporation is permitted.

Although the present invention has been described in considerable detailwith reference to certain aspects and embodiments thereof, other aspectsand embodiments are possible. Therefore, the spirit and scope of theappended claims should not be limited to the description of the versionscontained herein.

1. A film comprising: one or more propylene-based polymers having (i) 60wt % or more units derived from propylene, (ii) isotactically arrangedpropylene derived sequences, and (iii) a heat of fusion less than 65J/g; and one or more hydrocarbon resins each having a glass transitiontemperature greater than 20° C.
 2. The film of claim 1, wherein theamount of the hydrocarbon resin in the composition is sufficient toincrease intrinsic tear of the film by at least 20%.
 3. The film ofclaim 1, wherein the one or more propylene-based polymers has anethylene content of from 5 wt % to 16 wt %.
 4. The film of claim 1,wherein the one or more propylene-based polymers has a melt flow rate(230° C./2.16 Kg) of about 1 g/10 min to about 400 g/10 min.
 5. The filmof claim 1, wherein the propylene-based polymer has a density of atleast 0.80 g/cm³.
 6. The film of claim 1, wherein the propylene-basedpolymer has a melt temperature of less than 110° C.
 7. The film of claim1, wherein the hydrocarbon resin is a hydrogenated cycloaliphatic resin.8. The film of claim 1, wherein the hydrocarbon resin has a molecularweight (Mn) of from 200 to
 5000. 9. The film of claim 1, wherein thehydrocarbon resin has a softening point of from 80° C. to 180° C.
 10. Amethod for making a film composition, comprising: admixing one or morepropylene-based polymers and one or more miscible hydrocarbon resins inan amount sufficient to form a blend which provides a film having anincrease in intrinsic tear by at least 5% compared to a film withouteither the one or more propylene-based polymers or the one or moremiscible hydrocarbon resins, the propylene-based polymers each having(i) 60 wt % or more units derived from propylene, (ii) isotacticallyarranged propylene derived sequences, and (iii) a heat of fusion lessthan 45 J/g; and the hydrocarbon resins each having a glass transitiontemperature greater than 20° C.
 11. The method of claim 10, wherein theblend further comprises polypropylene or one or more thermoplasticresins.
 12. The method of claim 10, wherein the propylene-based polymeris present in the film in an amount of from 80 to 99 wt % and thehydrocarbon resin is present in an amount of from 1 to 20 wt %, based onthe total weight of the film.
 13. The method of claim 10, wherein theintrinsic tear of the film is at least 1.5 gm/micron.
 14. The method ofclaim 10, further comprising one or more styrenic block copolymers. 15.The method of claim 10, wherein the propylene-based polymer has a meltflow rate (230° C./2.16 Kg) of at least 3.0 g/10 min.
 16. The method ofclaim 10, wherein the propylene-based polymer has a density of at least0.80 g/cm³.
 17. The method of claim 10, wherein the propylene-basedpolymer has a melt temperature of less than 110° C.
 18. The method ofclaim 10, wherein the hydrocarbon resin is a hydrogenated cycloaliphaticresin.
 19. The method of claim 10, wherein the hydrocarbon resin has amolecular weight (Mn) of from 200 to
 5000. 20. The method of claim 10,wherein the hydrocarbon resin has a softening point of from 80° C. to180° C.
 21. A film comprising: one or more propylene-based polymershaving 60 wt % or more units derived from propylene, isotacticallyarranged propylene derived sequences, a heat of fusion less than 45 J/g,a density of at least 0.80 g/cm³, and a MFR of at least 3.0 g/10 min;and one or more hydrogenated cycloaliphatic resin each having amolecular weight (Mn) of from 200 to 5,000 and a glass transitiontemperature greater than 20° C., wherein the amount of the hydrocarbonresin in the composition is sufficient to increase intrinsic tear of thefilm by at least 5%.
 22. The film of claim 21, wherein the hydrocarbonresin has a softening point of from 125° C. to 140° C.
 23. The film ofclaim 1, further comprising polypropylene or one or more thermoplasticresins.
 24. The film of claim 1, wherein the propylene-based polymer ispresent in the film in an amount of from 80 to 99 wt % and thehydrocarbon resin is present in an amount of from 1 to 20 wt %, based onthe total weight of the film.
 25. The film of claim 1, wherein theintrinsic tear of the film is at least 1.5 gm/micron.